Devices and Methods for Performing Shear-Assisted Extrusion and Extrusion Processes

ABSTRACT

A method for preparing a shear-assisted extruded material from a powder billet is provided, the method comprising providing a billet of material in substantially powder form; applying both axial and rotational pressure to the material to deform at least some of the contacted material; and extruding the material to form an extruded material. A method for preparing shear-assisted extruded material is provided, the method comprising applying both axial and rotational pressure to stock material to form an extruded material at a rate between 2 and 13 m/min. A method for preparing shear-assisted extruded material is provided. The method comprises applying both axial and rotational pressure to stock material to form an extruded material; and aging the extruded material for less than 3 hours. A method for preparing shear-assisted extruded material is provided. The method comprises providing a stock material for shear-assisted extrusion; and applying both axial and rotational force to the stock material to form an extruded material, wherein the axial force does not decrease during the extrusion.

CROSS REFERENCE TO RELATED APPLICATION

This application claims priority to and the benefit of U.S. ProvisionalApplication Ser. No. 63/077,191 filed Sep. 11, 2020, the contents ofwhich are hereby incorporated by reference. This application is aContinuation-in-Part of and claims priority and the benefit of both U.S.Provisional Application Ser. No. 63/015,913 filed Apr. 27, 2020 and U.S.patent application Ser. No. 17/242,166 filed Apr. 27, 2021, which is aContinuation-in-Part of and claims priority to U.S. patent applicationSer. No. 17/033,854 filed Sep. 27, 2020, which is a Continuation-In-Partof and claims priority to U.S. patent application Ser. No. 16/562,314filed Sep. 5, 2019, which is a Continuation-In-Part of and claimspriority to U.S. patent application Ser. No. 16/028,173 filed Jul. 5,2018, now U.S. Pat. No. 11,045,851 issued Jun. 29, 2021, which is aContinuation-in-Part of and claims priority to U.S. patent applicationSer. No. 15/898,515 filed Feb. 17, 2018, now U.S. Pat. No. 10,695,811issued Jun. 30, 2020, which is a Continuation-in-Part and claimspriority and the benefit of both U.S. Provisional Application Ser. No.62/460,227 filed Feb. 17, 2017 and U.S. patent application Ser. No.15/351,201 filed Nov. 14, 2016, now U.S. Pat. No. 10,189,063 issued Jan.29, 2019, which is a Continuation-in-Part and claims priority and thebenefit of both U.S. Provisional Application Ser. No. 62/313,500 filedMar. 25, 2016 and U.S. patent application Ser. No. 14/222,468 filed Mar.21, 2014, which claims priority to and the benefit of U.S. ProvisionalApplication Ser. No. 61/804,560 filed Mar. 22, 2013; the contents of allof the foregoing are hereby incorporated by reference.

STATEMENT AS TO RIGHTS TO INVENTIONS MADE UNDER FEDERALLY-SPONSOREDRESEARCH AND DEVELOPMENT

This invention was made with Government support under ContractDE-AC05-76RL01830 awarded by the U.S. Department of Energy. TheGovernment has certain rights in the invention.

TECHNICAL FIELD

The present disclosure relates to metals technology in general, but morespecifically to extrusion and sheet metal technology.

BACKGROUND

Increased needs for fuel efficiency in transportation coupled with everincreasing needs for safety and regulatory compliance have focusedattention on the development and utilization of new materials andprocesses. In many instances, impediments to entry into these areas hasbeen caused by the lack of effective and efficient manufacturingmethods. For example, the ability to replace steel car parts withmaterials made from magnesium or aluminum or their associated alloys isof great interest. Additionally, the ability to form hollow parts withequal or greater strength than solid parts is an additional desired end.Previous attempts have failed or are subject to limitations based upon avariety of factors, including the lack of suitable manufacturingprocess, the expense of using rare earths in alloys to impart desiredcharacteristics, and the high energy costs for production.

What is needed is a process and device that enables the production ofitems such as components in automobile or aerospace vehicles with hollowcross sections that are made from materials such as magnesium oraluminum with or without the inclusion of rare earth metals. What isalso needed is a process and system for production of such items that ismore energy efficient, capable of simpler implementation, and produces amaterial having desired grain sizes, structure and alignment so as topreserve strength and provide sufficient corrosion resistance. What isalso needed is a simplified process that enables the formation of suchstructures directly from billets, powders or flakes of material withoutthe need for additional processing steps. What is also needed is a newmethod for forming high entropy alloy materials that is simpler and moreeffective than current processes. The present disclosure provides adescription of significant advance in meeting these needs.

Over the past several years researchers at the Pacific NorthwestNational Laboratory have developed a novel Shear Assisted Processing andExtrusion (ShAPE) technique which uses a rotating ram or die rather thana simply axially fed ram or die as is used in the conventional extrusionprocess. As described hereafter as well as in the in the previouslycited, referenced, and incorporated patent applications, this processand its associated devices provide a number of significant advantagesincluding reduced power consumption, better material properties andenables a whole new set of “solid phase” types of forming process andmachinery. Deployment of the advantages of these processes and devicesare envisioned in a variety of industries and applications including butnot limited to transportation, projectiles, high temperatureapplications, structural applications, nuclear applications, andcorrosion resistance applications.

Various additional advantages and novel features of the presentinvention are described herein and will become further readily apparentto those skilled in this art from the following detailed description. Inthe preceding and following descriptions we have shown and describedonly the preferred embodiment of the invention, by way of illustrationof the best mode contemplated for carrying out the invention. As will berealized, the invention is capable of modification in various respectswithout departing from the invention. Accordingly, the drawings anddescription of the preferred embodiment set forth hereafter are to beregarded as illustrative in nature, and not as restrictive.

Specific problems have hampered the metallurgic industry, for example,joining magnesium to aluminum can be troublesome because of theformation of brittle, Mg₁₇Al₁₂, intermetallics (IMC) at the dissimilarinterface. Conventional welding such as tungsten inert gas [1], electronbeam [2], laser [3], resistance spot [4] and compound casting [5] arenotorious for thick, brittle, Mg₁₇Al₁₂ interfacial layers since both theMg and Al go through melting and solidification.

In an effort to reduce the deleterious effects of Mg₁₇Al₁₂, manytechniques have been employed. For example, diffusion bonding,ultrasonic spot welding, electrical discharge riveting, and frictionstir approaches. Friction stir welding (FSW), and its many derivatives,has received some attention, but researches have yet to adequatelyaddress the fundamental problem of forming brittle Mg₁₇Al₁₂ interfaciallayers at the dissimilar interface.

Additionally, certain very useful materials such as Mg materials canhave an increased use if cost was less of a barrier. For example, in theautomotive industry, cost is the first major barrier for using Mg sheetmaterials. Unlike aluminum and steel, Mg alloys cannot be hot-rolledeasily in the as-cast condition due to a propensity for cracking. Assuch, Mg alloys are typically rolled by twin roll casting process or usea multi-step hot rolling, making the sheet forming process expensive.Cold rolling is even more susceptible to cracking and is thereforelimited to small reduction ratios (i.e. low throughput), which alsomakes the process slow and costly.

Referring to FIG. 1 , a brief description of traditional extrusion isshown in flow chart format. This traditional extrusion includes ingotformation, which is typically formed from mined material that isprepared in large ingots. Parts of these ingots are paired away and usedas extrusion starting material. Prior to extrusion, the ingots undergothermal process steps such as stress relief, phase conversion, andhomogenization. This homogenization can take place over several hours,if not days, and the homogenization requires the heating to extremetemperatures such as 490° C. as for example with aluminum alloy 7075. Asan example for AA7075, the ingots can be heated to this temperature overat least 11 hours, and then maintained at 430° C. for at least 20 hours.After homogenization, the material can be heated prior to extrusion. Theheating can include warming the material to significant temperatures,such as 300-530° C. to soften the material, and then pushing thematerial through a die to provide the extruded product that can then bewater quenched. Other alloy of aluminum, magnesium and many otherslisted in Table 1 also involve thermal treatments of billets prior toextrusion with each material in Table 1 requiring a time and temperaturesequence specific to the alloy being extruded. The extruded AA7075product can be solution heated at specific temperatures such as 450-480°C. for 30-120 minutes, and then the product can be artificially aged fora given amount of time at given temperatures that are specific to thematerial being heat treated. Aging can be performed for a minimum of 22hours at 120° C. according to the ASTM handbook. Other alloy ofaluminum, magnesium and many others listed in Table 1 also involvepost-extrusion solution heat treatment and artificial aging with eachmaterial in Table 1 requiring a time and temperature sequence specificto the alloy being extruded.

The present disclosure overcomes many of the requirement of the priorart by removing steps entirely and providing extruded materials that arehigher in quality than those prepared from these prior art methods.

SUMMARY

Shear-assisted extrusion processes for forming extrusions of a desiredcomposition from a feedstock material are provided. The processes caninclude applying a rotational shearing force and an axial extrusion tothe same location on the feedstock material using a die tool defined bya die face extending from a rim of the die face inwardly at an anglegreater than zero in relation to a sidewall of the tool in at least onecross section.

Devices for performing shear-assisted extrusion are provided. Thedevices can include a die tool defined by a die face extending from arim of the die face inwardly at an angle greater than zero in relationto a sidewall of the tool in at least one cross section.

Shear-assisted extrusion processes for forming extrusions of a desiredcomposition from a feedstock material are provided that can includeapplying a rotational shearing force and an axial extrusion to the samelocation on the feedstock material using a die tool defining an openingconfigured to receive feedstock material for extrusion and furtherdefining a die face defining a recess within the face and contiguouswith the opening.

Devices for performing shear-assisted extrusion are also provided thatcan include a die tool defining an opening configured to receivefeedstock material for extrusion and further defining a die facedefining a recess within the face and contiguous with the opening.

Shear-assisted extrusion process processes are also provided that caninclude: applying a rotational shearing force and an axial extrusionforce to the feedstock material using a die tool defining a die face andan opening within the die face configured to receive feedstock materialfor extrusion; mixing different portions of the feedstock materialwithin a recess about the opening prior to feedstock material enteringthe opening; and extruding the mixed portions.

The present description provides examples of shear-assisted extrusionprocesses for forming non-circular hollow-profile extrusions of adesired composition from feedstock material. At a high-level this isaccomplished by simultaneously applying a rotational shearing force andan axial extrusion force to the same location on the feedstock materialusing a scroll face with a plurality of grooves defined therein. Thesegrooves are configured to direct plasticized material from a firstlocation, typically on the interface between the material and the scrollface, through a portal defined within the scroll face to a secondlocation, typically upon a die bearing surface. At this location theseparated streams of plasticized material are recombined andreconfigured into a desired shape having the preselectedcharacteristics.

In some applications the scroll face has multiple portals, each portalconfigured to direct plasticized material through the scroll face and torecombine at a desired location either unified or separate. In theparticular application described the scroll face has two sets ofgrooves, one set to direct material from the outside in and anotherconfigured to direct material from the inside out. In some instances, athird set of grooves circumvolves the scroll face to contain thematerial and prevent outward flashing.

This process provides a number of advantages including the ability toform materials with better strength and corrosion resistancecharacteristics at lower temperatures, lower forces, and withsignificantly lower extrusion force and electrical power than requiredby other processes.

For example, in one instance the extrusion of the plasticized materialis performed at a die face temperature less than 150° C. In otherinstances the axial extrusion pressure is at or below 50 MPa. In oneparticular instance a magnesium alloy in billet form was extruded into adesired form in an arrangement wherein the axial extrusion pressure isat or below 25 MPa, and the temperature is less than 100° C. While theseexamples are provided for illustrative reasons, it is to be distinctlyunderstood that the present description also contemplates a variety ofalternative configurations and alternative embodiments.

Another advantage of the presently disclosed embodiment is the abilityto produce high quality extruded materials from a wide variety ofstarting materials including, billets, flakes powders, etc. without theneed for additional pre or post processing to obtain the desiredresults. In addition to the process, the present disclosure alsoprovides exemplary descriptions of a device for performingshear-assisted extrusion. In one configuration this device has a scrollface configured to apply a rotational shearing force and an axialextrusion force to the same preselected location on material wherein acombination of the rotational shearing force and the axial extrusionforce upon the same location cause a portion of the material toplasticize. The scroll face further has at least one groove and a portaldefined within the scroll face. The groove is configured to direct theflow of plasticized material from a first location (typically on theface of the scroll) through the portal to a second location (typicallyon the back side of the scroll and in some place along a mandrel thathas a die bearing surface) wherein the plasticized material recombinesafter passage through the scroll face to form an extruded materialhaving preselected features at or near these second locations.

This process provides for a significant number of advantages andindustrial applications. For example, this technology enables theextrusion of metal wires, bars, and tubes used for vehicle componentswith 50 to 100 percent greater ductility and energy absorption overconventional extrusion technologies, while dramatically reducingmanufacturing costs; this while being performed on smaller and lessexpensive machinery than what is used in conventional extrusionequipment. Furthermore, this process yields extrusions from lightweightmaterials like magnesium and aluminum alloys with improved mechanicalproperties that are impossible to achieve using conventional extrusion,and can go directly from powder, flake, or billets in just one singlestep, which dramatically reduces the overall energy consumption andprocess time compared to conventional extrusion.

Applications of the present processes and devices could, for example, beused to form parts for the front end of an automobile wherein it ispredicted that a 30 percent weight savings can be achieved by replacingaluminum components with lighter-weight magnesium, and a 75 percentweight savings can be achieved by replacing steel with magnesium.Typically processing into such embodiments have required the use of rareearth elements into the magnesium alloys to achieve properties suitablefor structural energy absorption applications. However, these rare earthelements are expensive and rare and in many instances are found in areasof difficult circumstances, making magnesium extrusions too expensivefor all but the most exotic vehicles. As a result, less than 1 percentof the weight of a typical passenger vehicle comes from magnesium. Theprocesses and devices described hereafter, however, enable the use ofnon-rare earth magnesium alloys to achieve comparable results as thosealloys that use the rare earth materials. This results in additionalcost saving in addition to a tenfold reduction in powerconsumption—attributed to significantly less force required to producethe extrusions—and smaller machinery footprint requirements.

As a result, the present technology could find ready adaptation in themaking of lightweight magnesium components for automobiles such as frontend bumper beams and crush cans. In addition to the automobile,deployments of the present invention can drive further innovation anddevelopment in a variety of industries such as aerospace, electric powerindustry, semiconductors and more. For example, this technique could beused to produce creep-resistant steels for heat exchangers in theelectric power industry, and high-conductivity copper and advancedmagnets for electric motors. It has also been used to producehigh-strength aluminum rods for the aerospace industry, with the rodsextruded in one single step, directly from powder, with twice theductility compared to conventional extrusion. In addition, thesolid-state cooling industry is investigating the use of these methodsto produce semiconducting thermoelectric materials.

The process of the present disclosure allows precise control overvarious features such as grain size and crystallographic orientation—characteristics that determine the mechanical properties of extrusions,like strength, ductility and energy absorbency. The technology producesa grain size for magnesium and aluminum alloys at an ultra-fine regime(<1 micrometer), representing a 10 to 100 times reduction compared tothe starting material. In magnesium, the crystallographic orientationcan be aligned away from the extrusion direction, which is what givesthe material such high energy absorption by eliminating anisotropybetween tensile and compressive strengths. A shift of 45 degrees hasbeen achieved, which is ideal for maximizing energy absorption inmagnesium alloys. Control over grain refinement and crystallographicorientation can be gained through adjustments to the geometry of thespiral groove, the spinning speed of the die, the amount of heatgenerated at the material-die interface and within the material, and theamount of force used to push the material through the die.

In addition, this extrusion process allows industrial-scale productionof materials with tailored structural characteristics. Unlike severeplastic deformation techniques that are only capable of bench-scaleproducts, ShAPE is scalable to industrial production rates, lengths, andgeometries. In addition to control of the grain size, an additionallayer of microstructural control has been demonstrated where grain sizeand texture can be tailored through the wall thickness oftubing—important because mechanical properties can now be optimized forextrusions depending on whether the final application experiencestension, compression, or internal pressure. This could make automotivecomponents more resistant to failure during collisions while using muchless material.

The process's combination of linear and rotational shearing results inup to 10 times lower extrusion force compared to conventional extrusion.This means that the size of hydraulic ram, supporting components,mechanical structure, and overall footprint can be scaled downdramatically compared to conventional extrusion equipment—enablingsubstantially smaller production machinery, lowering capitalexpenditures and operations costs. This process generates all the heatnecessary for producing extrusions via friction at the interface betweenthe system's billet and scroll-faced die and from plastic sheardeformation within the extruding material, thus not requiring thepre-heating and external heating used by other methods. This results indramatically reduced power consumption; for example, the 11 kW ofelectrical power used to produce a 2-inch diameter magnesium tube takesthe same amount of power to operate a residential kitchen oven—a ten- totwenty-fold decrease in power consumption compared to conventionalextrusion. Extrusion ratios up to 200:1 have been demonstrated formagnesium alloys using the described process compared to 50:1 forconventional extrusion, which means fewer to no repeat passes of thematerial through the machinery are needed to achieve the final extrusiondiameter—leading to lower production costs compared to conventionalextrusion.

Studies have shown a 10 times decrease in corrosion rate for extrudednon-rare earth ZK60 magnesium performed under this process compared toconventionally extruded ZK60. This is due to the highly refined grainsize and ability to break down, evenly distribute—and even dissolve—second-phase particles that typically act as corrosion initiation sites.The ShaPE process has also been used to clad magnesium extrusions withaluminum coating in order to reduce corrosion.

Shear-assisted extrusion processes for forming extrusions of a desiredcomposition from feedstock materials are also provided. The processescan include applying a rotational shearing force and an axial extrusionfrom to the same location on the feedstock material using a scrollhaving a scroll face. The scroll face can have an inner diameter portionbounded by an outer diameter portion, and a member extending from theinner diameter portion beyond a surface of the outer diameter portion.

Devices for performing shear-assisted extrusion are also provided. Thedevices can include a scroll having a scroll face having in innerdiameter portion bounded by an outer diameter portion, and a memberextending from the inner diameter portion beyond a surface of the outerdiameter portion.

Extrusion processes for forming extrusion of a desired composition fromfeedstock materials are also provided. The processes can include:providing feedstock for extrusion, with the feedstock comprising atleast two different materials. The process can include engaging thematerials with one another within a feedstock container, with theengaging defining an interface between the two different materials. Theprocess can continue by extruding the engaged feedstock materials toform an extruded product comprising a first portion comprising one ofthe two materials bound to a second portion comprising the other of thetwo materials. In accordance with example implementations, withextensive refinement, it has been shown that billet made from castingscan be extruded, in a single step, into high performance extrusions.

Extrusion feedstock materials are also provided that can includeinterlocked billets of feedstock materials. These interlocked billetscan be used for joining dissimilar materials and alloys, for example.

Methods for preparing metal sheets are also provided. The methods caninclude: producing a metal tube via shear assisted processing andextrusion; opening the metal tube to form a sheet having a firstthickness; and rolling the sheet to a second thickness that is less thanthe first thickness.

The present disclosure provides methods for producing an extrudedproduct from a solid billet. The methods can include providing anas-cast billet for extrusion; applying a simultaneous rotational shearand axial extrusion force to the as-cast billet to plasticize theas-cast billet; and extruding the plasticized as-cast billet with anextrusion die to form an extruded product.

Methods for preparing extruded products from billets can also include:providing a billet for extrusion; while maintaining a majority of thebillet below 100° C., applying a simultaneous rotational shear and axialextrusion force to one end of the billet to plasticize the one end ofthe billet; and extruding the plasticized one end of the billet with anextrusion die to form an extruded product.

Methods for preparing an extruded product from a billet can also includeproviding a billet for extrusion; applying a simultaneous rotationalshear and axial extrusion force to the billet to plasticize the billet;extruding the plasticized billet with an extrusion die to form anextruded product; and artificially aging the extruded product for lessthan 10 hours.

Various advantages and novel features of the present disclosure aredescribed herein and will become further readily apparent to thoseskilled in this art from the following detailed description. In thepreceding and following descriptions, exemplary embodiments of thedisclosure have been provided by way of illustration of the best modecontemplated for carrying out the disclosure. As will be realized, thedisclosure is capable of modification in various respects withoutdeparting from the disclosure. Accordingly, the drawings and descriptionof the preferred embodiment set forth hereafter are to be regarded asillustrative in nature, and not as restrictive.

The ShAPE processing and methods described herein may offer improvementsto transportation applications, such as automotive industries, in whichthe strength to weight ratio of advanced aluminum alloys (or otheralloys) is desirable. The methods and techniques described herein may beapplied to other non-aluminum material systems.

Methods for preparing shear-assisted extruded materials from powderbillets are provided. The methods can include providing a billet ofmaterial in substantially powder form; applying both axial androtational pressure to the material to deform at least some of thematerial; and extruding the material to form an extruded product.

Methods for preparing shear-assisted extruded materials are provided.The methods can include applying both axial and rotational pressure tostock material to form extruded material at a rate, for example, between2 and 13 m/min or higher speed.

Methods for preparing shear-assisted extruded materials are provided.The methods can include applying both axial and rotational pressure tostock material to form an extruded material; and aging the extrudedmaterial down to 3 hours or less.

Methods for preparing shear-assisted extruded materials are provided.The methods can include providing stock materials for shear-assistedextrusion; and applying both axial and rotational force to the stockmaterial to form extruded material without decreasing the axial forceduring the extrusion.

DRAWINGS

Embodiments of the disclosure are described below with reference to thefollowing accompanying drawings.

FIG. 1 provides a general overview of the state of the art of extrusionthat includes ingot formation, stress relief, phase conversion,homogenization, billet pre-heating, extrusion, solution heating, andaging.

FIG. 2A shows a ShAPE setup for extruding hollow cross section pieces.

FIG. 2B shows another configuration for extruding hollow cross-sectionalpieces.

FIG. 3A shows a top perspective view of a modified scroll face tool fora portal bridge die.

FIG. 3B shows a bottom perspective view of a modified scroll face thatoperates like a portal bridge die.

FIG. 3C shows a side view of the modified portal bridge die.

FIG. 4 shows an illustrative view of material separated using at leastsome of the devices shown in FIGS. 2A-3C.

FIG. 5A shows a ShAPE set up for consolidating high entropy alloys(HEAs) from arc melted pucks into densified pucks.

FIG. 5B shows an example of the scrolled face of the rotating tool inFIG. 5A.

FIG. 5C shows an example of HEA arc melted samples crushed and placedinside the chamber of the ShAPE device prior to processing.

FIG. 6 shows back scatter electron—scanning electron microscope(BSE-SEM) image of cross section of the HEA arc melted samples beforeShAPE processing, showing porosity, intermetallic phases and cored,dendritic microstructure.

FIG. 7A shows BSE-SEM images at the bottom of the puck resulting fromthe processing of the material in FIG. 5C.

FIG. 7B shows BSE-SEM images halfway through the puck

FIG. 7C shows BSE-SEM images of the interface between high shear regionun-homogenized region (approximately 0.3 mm from puck surface)

FIG. 7D shows BSE-SEM images of a high shear region

FIG. 8 is a depiction of a series of different die face configurationsaccording to embodiments of the disclosure.

FIG. 9 is an isometric view of a die face tool according to anembodiment of the disclosure.

FIGS. 10A-10C are depictions of a die face according to an embodiment ofthe disclosure.

FIGS. 11A-11C are depictions of a die face according to an embodiment ofthe disclosure.

FIGS. 12A-12C are depictions of a die face according to an embodiment ofthe disclosure.

FIGS. 13A-13C are depictions of a die face according to an embodiment ofthe disclosure.

FIGS. 14A-14C are depictions of a die face according to an embodiment ofthe disclosure.

FIGS. 15A-15B are depictions of the use of a die face on startingmaterials according to an embodiment of the disclosure.

FIG. 16 is a depiction of the use of a die face on starting materialaccording to an embodiment of the disclosure.

FIG. 17 is a depiction of a die according to an embodiment of thedisclosure.

FIG. 18 is a depiction of extruded material as well as a remnant of thestarting material according to an embodiment of the disclosure.

FIG. 19 is a depiction of a die according to an embodiment of thedisclosure.

FIG. 20 is a depiction of a die according to an embodiment of thedisclosure. Die for purposes of this disclosure refers to scroll face orincorporated die, for example.

FIG. 21 is data demonstrating reduced extrusion force utilizing dieconfigurations of the present disclosure.

FIG. 22 is a depiction of data depicting reduced motor torque utilizingdies of the present disclosure.

FIG. 23 is a depiction of two dies, one having a flat face and onehaving a conical face according to an embodiment of the disclosure.

FIG. 24 is a depiction of data demonstrating reduced force utilizingdies according to an embodiment of the disclosure.

FIG. 25 again is data demonstrating reduced torque utilizing diesaccording to an embodiment of the disclosure.

FIG. 26 is a depiction of data demonstrating reduced temperatureutilizing dies according to an embodiment of the disclosure.

FIG. 27 is a depiction of dies corresponding to extruded materialsaccording to an embodiment of the disclosure.

FIGS. 28-29 are depictions of dies corresponding to extruded materialsaccording to an embodiment of the disclosure.

FIGS. 30-31 depict extruded product materials utilizing different diesaccording to an embodiment of the disclosure.

FIG. 32 is a die according to an embodiment of the disclosure.

FIG. 33 is another die according to an embodiment of the disclosure.

FIG. 34 is a depiction of extruded materials produced utilizing diesaccording to an embodiment of the disclosure.

FIG. 35 is data for different dies according to an embodiment of thedisclosure.

FIG. 36 is data acquired utilizing dies according to an embodiment ofthe disclosure.

FIG. 37 is a series of photographs of extrusion of Mg—Al withconsolidated cross sections, and in (B) showing gradient in compositionbetween Mg and Al with absence of a Mg₁₇Al₁₂ interfacial layer atdissimilar interface (C).

FIG. 38 is a depiction of an example extrusion assembly according to anembodiment of the disclosure and also a depiction of feedstock materialengagements and/or feedstock interfaces according to an embodiment ofthe disclosure.

FIG. 39 is a depiction of extruded material having no Mg₁₇Al₁₂interfacial layer.

FIG. 40 is a depiction of extrusion material having a graded interfacelayer prepared using engaged feedstock materials according to anembodiment of the disclosure.

FIG. 41 is a depiction of two components, AA7075 and AA6061, bonded atan abrupt transition layer according to an embodiment of the disclosure.

FIG. 42 is an example rolling mill assembly according to an embodimentof the disclosure.

FIG. 43 demonstrates the process steps for preparing an extrudedfabricated tube, the open tube, and the rolling of the tube according toan embodiment of the disclosure.

FIGS. 44A and 44B depict an example extrusion assembly according to anembodiment of the disclosure as well as example extruded materialaccording to an embodiment of the disclosure.

FIG. 45 demonstrates the process steps for preparing a metal sheetthrough to 16 passes according to an embodiment of the disclosure.

FIG. 46 demonstrates a 0.005 inch thick sheet in various configurationsaccording to an embodiment of the disclosure.

FIG. 47 shows reduction per rolling pass according to an embodiment ofthe disclosure.

FIGS. 48A-48C demonstrate front end methods of preparing billets forextrusion. These methods are shown in FIG. 48A with ingot formation,stress relief, phase conversion, billet pre-heating, and extrusion; FIG.48B with ingot formation, stress relief, phase conversion,homogenization, and extrusion; and FIG. 48C with ingot formation andextrusion.

FIGS. 49A and 49B depict prior art methods of billet homogenizationaccording to ASTM methods. As shown, a substantial amount of the time,at least 20 hours, is removed from the homogenization step.

FIG. 50 is data of extruded product according to embodiments of thepresent disclosure.

FIG. 51 is depiction of extruded product according to embodiments of thepresent disclosure.

FIG. 52 is a stepwise depiction of extrusion and solution heatingaccording to embodiments of the present disclosure.

FIG. 53 is data acquired utilizing methods according to embodiments ofthe present disclosure.

FIG. 54 is data acquired utilizing methods according to embodiments ofthe present disclosure.

FIG. 55 is data acquired utilizing methods according to embodiments ofthe present disclosure.

FIGS. 56A-56B depict extrusion to aging techniques and extrusionsolution heating and aging techniques according to embodiments of thepresent disclosure.

FIG. 57 depicts data acquired utilizing methods according to embodimentsof the present disclosure.

FIG. 58 depicts material change upon application of ShAPE to powder Alaccording to an embodiment of the disclosure.

FIG. 59 depicts another view of material change upon application ofShAPE to powder Al according to an embodiment of the disclosure.

FIG. 60 depicts views of material changes upon application of ShAPE topowder Al, Fe, Ti and Cr according to an embodiment of the disclosure.

FIG. 61 depicts ShAPE axial forces in the context of traditionalextrusion forces with “No Breakthrough” indicating the breakthroughforce that is eliminated with ShAPE.

FIG. 62 depicts ShAPE rotational rpms and axial forces of ShAPE.

FIG. 63 depicts Aluminum (AA 6063) ShAPE processes parameters.

FIG. 64 depicts Aluminum (AA 7075) ShAPE processes parameters.

FIG. 65 depicts alloy (Mg ZK60) ShAPE processes parameters.

DESCRIPTION

This disclosure is submitted in furtherance of the constitutionalpurposes of the U.S. Patent Laws “to promote the progress of science anduseful arts” (Article 1, Section 8).

The following description including the attached pages provide variousexamples of the present invention. It will be clear from thisdescription of the invention that the invention is not limited to theseillustrated embodiments but that the invention also includes a varietyof modifications and embodiments thereto. Therefore, the presentdescription should be seen as illustrative and not limiting. While theinvention is susceptible to various modifications and alternativeconstructions, it should be understood, that there is no intention tolimit the invention to the specific form disclosed, but, on thecontrary, the invention is to cover all modifications, alternativeconstructions, and equivalents falling within the spirit and scope ofthe invention as defined in the claims.

In the previously described and related applications various methods andtechniques are described wherein the described technique and device(referred to as ShAPE) is shown to provide a number of significantadvantages including the ability to control microstructure such ascrystallographic texture through the cross sectional thickness, whilealso providing the ability to perform various other tasks. In thisdescription we provide information regarding the use of the ShAPEtechnique to form materials with non-circular hollow profiles as well asmethods for creating high entropy alloys that are useful in a variety ofapplications such as projectiles. Exemplary applications will bediscussed on more detail in the following.

Referring first now to FIGS. 2A and 2B, examples of the ShAPE device andarrangement are provided. In an arrangement such as the one shown inFIG. 2A, rotating die 10 is thrust into a material 20 under specificconditions whereby the rotating and shear forces of the die face 12 andthe die plunge 16 combine to heat and/or plasticize the material 20 atthe interface of the die face 12 and the material 20 and cause theplasticized material to flow in desired direction in either a direct orindirect manner. (In other embodiments the material 20 may spin and thedie 10 pushed axially into the material 20 so as to provide thiscombination of forces at the material face.) In either instance, thecombination of the axial and the rotating forces plasticize the material20 at the interface with the die face 12. Flow of the plasticizedmaterial can then be directed to another location wherein a die bearingsurface 24 of a preselected length facilitates the recombination of theplasticized material into an arrangement wherein a new and more refinedgrain size and texture control at the micro level can take place. Thisthen translates to an extruded product 22 with desired characteristics.This process enables better strength, ductility, and corrosionresistance at the macro level together with increased and betterperformance. This process can eliminate the need for additional heating,and the process can utilize a variety of forms of material includingbillet, powder or flake without the need for extensive preparatoryprocesses such as “steel canning”, billet pre-heating, de-gassing,de-canning and other process steps can be utilized as well. Thisarrangement also provides for a methodology for performing other stepssuch as cladding, enhanced control for through wall thickness and othercharacteristics, joining of dissimilar materials and alloys, andbeneficial feedstock materials for subsequent rolling operations.

This arrangement is distinct from and provides a variety of advantagesover the prior art methods for extrusion. First, during the extrusionprocess the force rises to a peak in the beginning and then falls offonce the extrusion starts. This is called breakthrough. In this ShAPEprocess the temperature at the point of breakthrough is very low. Forexample for Mg tubing, the temperature at breakthrough for the 2″ OD, 75mil wall thickness ZK60 tubes is <150 C. This lower temperaturebreakthrough is believed in part to account for the superiorconfiguration and performance of the resulting extrusion products.

Another feature is the low extrusion coefficient kf which describes theresistance to extrusion (i.e. lower kf means lower extrusionforce/pressure). Kf is calculated to be 2.55 MPa and 2.43 MPa for theextrusions made from ZK60-T5 bar and ZK60 cast respectively (2″ OD, 75mil wall thickness). The ram force and kf are remarkably low compared toconventionally extruded magnesium where kf ranges from 68.9-137.9 MPa.As such, the ShAPE process achieved a 20-50 times reduction in kf (asthus ram force) compared to conventional extrusion. This assists notonly with regard to the performance of the resulting materials but alsoreduced energy consumption required for fabrication. For example, theelectrical power required to extrude the ZK60-T5 bar and ZK60 cast (2″OD, 750 mil wall thickness) tubes is 11.5 kW during the process. This ismuch lower than a conventional approach that uses heatedcontainers/billets. Similar reductions in kf have also been observedwhen extruding high performance aluminum powder directing into wire,rod, and tubing.

The ShAPE process is significantly different than Friction Stir BackExtrusion (FSBE). In FSBE, a spinning mandrel is rammed into a containedbillet, much like a drilling operation. Scrolled grooves force materialoutward and material back extrudes around and onto the mandrel to form atube, not having been forced through a die. As a result, only very smallextrusion ratios are possible, the tube is not fully processed throughthe wall thickness, the extrudate is not able to push off of themandrel, and the tube length is limited to the length of the mandrel. Incontrast, ShAPE utilizes spiral grooves on a die face to feed materialinward through a die and around a mandrel that is traveling in the samedirection as the extrudate. As such, a much larger outer diameter andextrusion ratio are possible, the material is uniformly process throughthe wall thickness, the extrudate is free to push off the mandrel as inconventional extrusion, and the extrudate length is only limited only bythe starting volume of the billet. ShAPE can be scalable to themanufacturing level, while the limitations of FSBE have kept thetechnology as a non-scalable academic interest since FBSE was firstreported.

An example of an arrangement using a ShAPE device and a mandrel 18 isshown in FIG. 2B. This device and associated processes have thepotential to be a low-cost, manufacturing technique to fabricate varietyof materials. As will be described below in more detail, in addition tomodifying various parameters such as feed rate, heat, pressure and spinrates of the process, various mechanical elements of the tool assist toachieve various desired results. For example, varying scroll patterns 14on the face of extrusion dies 12 can be used to affect/control a varietyof features of the resulting materials. This can include control ofgrain size and crystallographic texture along the length of theextrusion and through-wall thickness of extruded tubing and otherfeatures. Alteration of parameters can be used to advantageously alterbulk material properties such as ductility and strength and allowtailoring for specific engineering applications including altering theresistance to crush, pressure or bending. Scrolls patterns have alsobeen found to affect grain size and texture through the thickness of theextrusion.

The ShAPE process has been utilized to form various structures from avariety of materials including the arrangement as described in thefollowing table.

TABLE 1 Alloy Material Class Precursor Form PUCKS Bi₂Te₃ ThermoelectricPowder Fe—Si Magnet Powder Nd₂Fe₁₁B/Fe Magnet Powder Nd₂Fe₁₄B MagnetPowder MA956 ODS Steel Powder Nb 0.95 Ti 0.05 Thermoelectric Powder Fe 1Sb 1 Mn—Bi Magnet Powder Al—Si Model Binary Alloy Powder Cu—Ni ModelBinary Alloy Powder Cu—Nb Model Binary Alloy Powder PM 2000 ODS SteelPowder Eurofer 97 ODS Steel Powder 14YWT ODS Steel Powder TUBES ZK60Magnesium Alloy Barstock, Casting AZ31 Magnesium Alloy Barstock AZ91Magnesium Alloy Flake, Casting AZS312 Magnesium Alloy Casting Mg-7 wt %Si Magnesium Alloy Casting AZ91- 1, 5 and 10 Mg MMC Mechanically wt. %Al₂O₃ Alloyed Flake AZ91- 1, 5 and 10 Mg MMC Mechanically wt. % Y₂O₃Alloyed Flake AZ91- 1, 5 and 10 Mg MMC Mechanically and 5 wt. % SiCAlloyed Flake AA2024 Structural Aluminum Cast, Barstock AA6061Structural Aluminum Cast, Barstock AA6063 Structural Aluminum Casting,Barstock and Chip AA7075 High Strength Aluminum Casting, barstockAl-12.4TM High Strength Aluminum Powder A356 Structural Aluminum ChipAA2024/1100 Aluminum Cladding Casting, barstock AA7075/AA6061 AluminumCladding Casting, barstock 1100/7075/1100 Aluminum Cladding Casting,barstock RODS Al—Mn wt. 15% Aluminum Manganese Casting Alloy Al—Mg Mg AlCoextrusion Barstock Mg—Dy—Nd—Zn—Zr Magnesium Rare Earth Barstock CuPure Copper Barstock ODS-Cu Oxide Dispersion Powder Strengthened CuCu-Graphite Conductive Copper Powder Cu-Graphene Conductive CopperPowder + Film Cu-Graphene Conductive Copper Barstock + Film Cu-GrapheneConductive Copper Foil + Film Al-Graphene Conductive Aluminum Powder +Film Al-Reduced Graphene Conductive Aluminum Barstock + FlakeAl-Graphite Conductive Aluminum Barstock + Powder CP-Mg Pure MagnesiumBarstock, casting AA6061 Aluminum Casting, barstock AA7075 AluminumCasting, barstock Al—Ti—Mg—Cu—Fe High Entropy Alloy Casting Al- 1, 5, 10at. % Mg Magnesium Alloy Casting Al-12.4TM High Temperature/ PowderStrength Aluminum Rhodium Pure Rhodium Barstock Al—Ce High Temperature/Casting Strength Aluminum AA1100 Aluminum Alloy Barstock AA7XXX HighStrength Aluminum Proprietary Powder 14YWT ODS Steel Powder MA956 ODSSteel Powder Bi₂Te₃ Thermoelectric Casting and Sintered Powder MixedPlastic Plastic Scrap and Pellets

In addition, to the pucks, rods and tubes described above, the presentdisclosure also provides a description of the use of a speciallyconfigured scroll component referred by the inventors as a portal bridgedie head which allows for the fabrication of ShAPE extrusions withnon-circular hollow profiles. This configuration allows for makingextrusion with non-circular, and multi-zoned, hollow profiles using aspecially formed portal bridge die and related tooling.

FIGS. 3A-3C show various views of a portal bridge die design with amodified scroll face that unique to operation in the ShAPE process. FIG.3A shows an isometric view of the scroll face on top of the portalbridge die and FIG. 3B shows an isometric view of the bottom of theportal bridge die with the mandrel visible.

In the present embodiment grooves 13, 15 on the face 12 of the die 10direct plasticized material toward the aperture ports 17. Plasticizedmaterial then passes through the aperture ports 12 wherein it isdirected to a die bearing surface 24 within a weld chamber similar toconventional portal bridge die extrusion. In this illustrative example,material flow is separated into four distinct streams using four ports17 as the billet and the die are forced against one another whilerotating.

While the outer grooves 15 on the die face feed material inward towardthe ports 17, inner grooves 13 on the die face feed material radiallyoutward toward the ports 17. In this illustrative example, one groove 13is feeding material radially outward toward each port 17 for a total offour outward flowing grooves. The outer grooves 15 on the die surface 12feed material radially inward toward the port 17. In this illustrativeexample, two grooves are feeding material radially inward toward eachport 17 for a total of eight inward feeding grooves 15. In addition tothese two sets of grooves, a perimeter groove 19 on the outer perimeterof the die, shown in FIG. 3C, is oriented counter to the die rotation soas to provide back pressure thereby minimizing material flash betweenthe container and die during extrusion.

FIG. 3B shows a bottom perspective view of the portal bridge die 12. Inthis view, the die shows a series of full penetration of ports 17. Inuse, streams of plasticized material funneled by the inward 15 andoutward 13 directed grooves described above pass through thesepenetration portions 17 and then are recombined in a weld chamber 21 andthen flow around a mandrel 18 to create a desired cross section. The useof scrolled grooves 13, 15, 19 to feed the ports 17 during rotation—as ameans to separate material flow of the feedstock (e.g. powder, flake,billet, etc.) into distinct flow streams has never been done to ourknowledge. This arrangement enables the formation of items withnoncircular hollow cross sections.

FIG. 4 shows a separation of magnesium alloy ZK60 into multiple streamsusing the portal bridge die approach during ShAPE processing. (In thiscase the material was allowed to separate for effect and illustration ofthe separation features and not passed over a die bearing surface forcombination). Conventional extrusion does not rotate and the addition ofgrooves would greatly impede material flow. But when rotation ispresent, such as in ShAPE or friction extrusion, the scrolls not onlyassist flow, but significantly assist the functioning of a portal bridgedie extrusion 17 and the subsequent formation of non-circular hollowprofile extrusions. Without scrolled grooves feeding the portals,extrusion via the portal bridge die approach using a process whererotation is involved, such as ShAPE, would be ineffective for makingitems with such a configuration. The prior art conventional linearextrusion process teach away from the use of surface features to guidematerial into the portals 17 during extrusion.

In the previously described and related applications various methods andtechniques are described wherein the ShAPE technique and device is shownto provide a number of significant advantages including the ability tocontrol microstructure such as crystallographic texture through thecross sectional thickness, while also providing the ability to performvarious other tasks. In this description we provide informationregarding the use of the ShAPE technique to form materials withnon-circular hollow profiles as well as methods for creating highentropy alloys that are useful in a variety of applications. These twoexemplary applications will be discussed on more detail in thefollowing.

FIG. 5A shows a schematic of the ShAPE process which utilizes a rotatingtool to apply load/pressure and at the same time the rotation helps inapplying torsional/shear forces, to generate heat at the interfacebetween the tool and the feedstock and within the material, thus helpingto consolidate the material. In this particular embodiment thearrangement of the ShAPE setup is configured so as to consolidate highentropy alloy (HEA) arc-melted buttons into densified pucks. In thisarrangement the rotating ram tool is made from an Inconel alloy and hasan outer diameter (OD) of 25.4 mm, and the scrolls on the ram face were0.5 mm in depth and had a pitch of 4 mm with a total of 2.25 turns. Inthis instance the ram surface incorporated a thermocouple to record thetemperature at the interface during processing. (see FIG. 5B) The setupenables the ram to spin at speeds from 25 to 1500 RPM.

In use, both an axial force and a rotational force are applied to amaterial of interest causing the material to plasticize. In extrusionapplications, the plasticized material then flows over a die bearingsurface dimensioned so as to allow recombination of the plasticizedmaterials in an arrangement with superior grain size distribution andalignment than what is possible in traditional extrusion processing. Asdescribed in the prior related applications this process provides anumber of advantages and features that conventional prior art extrusionprocessing is simply unable to achieve.

High entropy alloys are generally solid-solution alloys made of five ormore principal elements in equal or near equal molar (or atomic) ratios.While this arrangement can provide various advantages, it also providesvarious challenges particularly in forming. While conventional alloyscan comprise one principal element that largely governs the basicmetallurgy of that alloy system (e.g. nickel-base alloys, titanium-basealloys, aluminum-base alloys, etc.) in an HEA each of the five (or more)constituents of HEAs can be considered as the principal element.Advances in production of such materials may open the doors to theireventual deployment in various applications. However, standard formingprocesses have demonstrated significant limitations in this regard.Utilization of the ShAPE type of process demonstrates promise inobtaining such a result.

In one example a “low-density” AlCuFe(Mg)Ti HEA was formed. Beginningwith arc-melted alloy buttons as a pre-cursor, the ShAPE process wasused to simultaneously heat, homogenize, and consolidate the HEAresulting in a material that overcame a variety of problems associatedwith prior art applications and provided a variety of advantages. Inthis specific example, HEA buttons were arc-melted in a furnace under10⁻⁶ Torr vacuum using commercially pure aluminum, magnesium, titanium,copper and iron. Owing to the high vapor pressure of magnesium, amajority of magnesium vaporized and formed Al1Mg0.1Cu2.5Fe1Ti1.5 insteadof the intended Al1Mg1Cu1Fe1Ti1 alloy. The arc melted buttons describedin the paragraph above were easily crushed with a hammer and used tofill the die cavity/powder chamber (FIG. 5C), and the shear-assistedextrusion process initiated. The volume fraction of the material filledwas less than 75%, but was consolidated when the tool was rotated at 500RPM under load control with a maximum pressure set at 85 MPa and at 175MPa.

Comparison of the arc-fused material and the materials developed underthe ShAPE process demonstrated various distinctions. The arc meltedbuttons of the LWHEA exhibited a cored dendritic microstructure alongwith regions containing intermetallic particles and porosity. Using theShAPE process these microstructural defects were eliminated to form asingle phase, refined grain and no porosity LWHEA sample

FIG. 6 shows the backscattered SEM (BSE-SEM) image of theas-cast/arc-melted sample. The arc melted samples had a cored dendriticmicrostructure with the dendrites rich in iron, aluminum and titaniumand were 15-30 μm in diameter, whereas the inter-dendritic regions wererich in copper, aluminum and magnesium. Aluminum was uniformlydistributed throughout the entire microstructure. Such microstructuresare typical of HEA alloys. The inter-dendritic regions appeared to berich in Al—Cu—Ti intermetallic and was verified by XRD as AlCu₂Ti. XRDalso confirmed a Cu₂Mg phase which was not determined by the EDSanalysis and the overall matrix was BCC phase. The intermetallics formeda eutectic structure in the inter-dendritic regions and wereapproximately 5-10 μm in length and width. The inter-dendritic regionsalso had roughly 1-2 vol % porosity between them and hence was difficultto measure the density of the same.

Typically such microstructures are homogenized by sustained heating forseveral hours to maintain a temperature near the melting point of thealloy. In the absence of thermodynamic data and diffusion kinetics forsuch new alloy systems the exact points of various phase formations orprecipitation is difficult to predict particularly as related to varioustemperatures and cooling rates. Furthermore, unpredictability withregard to the persistence of intermetallic phases even after the heattreatment and the retention of their morphology causes furthercomplications. A typical lamellar and long intermetallic phase istroublesome to deal with in conventional processing such as extrusionand rolling and is also detrimental to the mechanical properties(elongation).

The use of the ShAPE process enabled refinement of the microstructurewithout performing homogenization heat treatment and provides solutionsto the aforementioned complications. The arc melted buttons, because ofthe presence of their respective porosity and the intermetallic phases,were easily fractured into small pieces to fill in the die cavity of theShAPE apparatus. Two separate runs were performed as described in Table1 with both the processes' yielding a puck with diameter of 25.4 mm andapproximately 6 mm in height. The pucks were later sectioned at thecenter to evaluate the microstructure development as a function of itsdepth. Typically in the ShAPE consolidation process; the shearing actionis responsible for deforming the structure at interface and increasingthe interface temperature; which is proportional to the rpm and thetorque; while at the same time the linear motion and the heat generatedby the shearing causes consolidation. Depending on the time of operationand force applied near through thickness consolidation can also beattained.

TABLE 2 Consolidation processing conditions utilized for LWHEA PressureProcess Run # (MPa) Tool RPM Temperature Dwell Time 1 175 500 180 s 2 85500 600° C. 180 s

FIGS. 7A-7D show a series of BSE-SEM images ranging from the essentiallyunprocessed bottom of the puck to the fully consolidated region at thetool billet interface. There is a gradual change in microstructure fromthe bottom of the puck to the interface where shear was applied. Thebottom of the puck had the microstructure similar to one described inFIG. 6 . But as the puck is examined moving towards the interface thesize of these dendrites become closely spaced (FIG. 7B). Theintermetallic phases are still present in the inter-dendritic regionsbut the porosity is completely eliminated. On the macro scale the puckappears more contiguous and without any porosity from the top to thebottom ¾^(th) section. FIG. 7C shows the interface where the shearingaction is more prominent. This region clearly demarcates the as-castcast dendritic structure to the mixing and plastic deformation caused bythe shearing action. A helical pattern is observed from this region tothe top of the puck. This is indicative of the stirring action and dueto the scroll pattern on the surface of the tool. This shearing actionalso resulted in the comminution of the intermetallic particles and alsoassisted in the homogenizing the material as shown in FIGS. 7C and 7D.It should be noted that this entire process lasted only 180 seconds tohomogenize and uniformly disperse and comminute the intermetallicparticles. The probability that some of these intermetallic particleswere re-dissolved into the matrix is very high. The homogenized regionwas nearly 0.3 mm from the surface of the puck.

The use of the ShAPE device and technique demonstrated a novel singlestep method to process without preheating of the billets. The timerequired to homogenize the material was significantly reduced using thisnovel process. Based on the earlier work, the shearing action and thepresence of the scrolls helped in comminution of the secondary phasesand resulted in a helical pattern. All this provides significantopportunities towards cost reduction of the end product withoutcompromising the properties and at the same time tailoring themicrostructure to the desired properties. Similar acceleratedhomogenization has also been observed in magnesium and aluminum alloysduring ShAPE of as-cast materials.

In as much as types of alloys exhibit high strength at room temperatureand at elevated temperature, good machinability, high wear and corrosionresistance, such materials could be seen as a replacement in a varietyof applications. A refractory HE-alloy could replace expensivesuper-alloys used in applications such as gas turbines and the expensiveInconel alloys used in coal gasification heat exchanger. A light-weightHE-alloy could replace aluminum and magnesium alloys for vehicles andairplanes. Use of the ShAPE process to perform extrusions would enablethese types of deployments.

Referring next to FIG. 8 , a device for performing shear-assistedextrusion is disclosed with reference to different implementations A, B,and C. In accordance with example implementations, device 100 can be ascroll having a scroll face 110 that includes an inner diameter portion104 as well as outer diameter portions 106. Accordingly, these 3 scrollfaces are shown in accordance with one cross section. As shown anddepicted herein, viewed from the face they would have a circularformation. Accordingly, inner diameter portion 104 can extend beyond asurface 110 of outer diameter portion 106. Devices 100 can includeapertures 115 arranged within the outer diameter portion and extendingthrough the device. As shown and depicted, inner portion 104, as well as114 and 116 can be defined by the member extending from surface 110. Inaccordance with alternative implementations, this member may not occupyall of inner portion 104, but only a portion. In accordance with exampleimplementations, portion 104 can be rectangular in one cross section,and with reference implementation B, portion 114 can be trapezoidal inone cross section, and with reference to implementation C, portion 116can be conical in one implementation. In each of these implementations,the member can have sidewalls, and these sidewalls can define structuresthereon, for example, these structures can be groves and/or extensionsthat provide for the transition of material away towards the perimeterof the scroll face, which then would direct the material being processedthrough apertures 115.

Referring next to FIG. 9 , an example scroll face device is depicted inisometric view having inner portion 104 and outer portion 106.Accordingly, the device can include raised portions 140, 142, and/or144. These portions can provide for a flow of material in predetermineddirection. For example, portions 140 can be configured to providematerial to within apertures 115, while portions 142 can be configuredto provided material to within the same apertures 115, thereby providingfor flow of materials toward one another. Portions 144 can be providedfor mechanicals needs as the device is utilized.

In accordance with example implementations, Shear assisted processingand extrusion (ShAPE™) can be used to join magnesium and aluminum alloysin a butt joint configuration. Joining can occur in the solid-phase andin the presence of shear, brittle Mg₁₇Al₁₂ intermetallic layers can beeliminated from the Mg—Al interface. The joint composition cantransition gradually from Mg to Al, absent of Mg₁₇Al₁₂, which canimprove mechanical properties compared to joints where Mg₁₇Al₁₂interfacial layers are present.

As alluded to joining Mg—Al is difficult to perform without forming abrittle Mg₁₇Al₁₂ interfacial layer at the dissimilar interface. Exampleapplications for material having been joined using the processes of thepresent disclosure include, but are not limited to:

-   -   Lightweight of rivets and bolts (i.e. Al shank with Mg head or        vice versa)    -   Multi-material extrusion for structural members (tailor welded        extrusions)    -   Mg—Al tailor welded blanks formed by slitting and rolling        thin-walled tubes    -   Corrosion resistant joints due to galvanically graded Mg—Al        interface    -   Dissimilar Mg alloy or Al alloy joint pairs (i.e. AA6061 to        AA7075) Referring to FIGS. 10A-10C, different views of a scroll        face or die face of an extrusion die tool are shown including        cross sectional views. In accordance with example        implementations, the die tool can also be configured with or        without scrolls in the die face. For example, when processing        high temperature materials like steels, Tungsten Rhenium can be        used as the die tool material. This material can engage the        feedstock material to the extent that friction or shear is        provided thereby producing sufficient deformational heating.

Die tool 200 can include tool sidewalls 202 as well as die face rim 204.In FIG. 10B, die face 208 can have an opening 206 configured to receiveand extrude feedstock material mixed and provided during the process.Referring next to FIG. 10C, from opening 206 can extend die face 208. Asshown, die face 208 can be extended at an angle in relation to rim 204or sidewall 202. This angle can be greater than zero degrees as shown intable 3; as an example for tubes fabricated with 12 mm outer diameterand 1 mm and 2 mm wall thickness. In accordance with exampleimplementations this angle can form a portion of the die face, asubstantial portion of the die face (for example extending greater than50% of the radius of the die face), and/or an entirety of the die facefrom rim 204 to opening 206.

TABLE 3 Extrusions fabricated with differing degrees of angled scrollfaces. Wall Thickness 6 Scroll 1 and 2 mm 4 Scroll, 0 deg 1 and 2 mm 4Scroll, 14 deg 1 and 2 mm 4 Scroll, 26 deg 1 and 2 mm 4 Scroll, 45 deg 1and 2 mm

Referring next to FIG. 11A, in accordance with another exampleimplementation, die 200 can have an outer rim 204 can have a portionthat is substantially planar in relation to face 208 thereby providing asubstantially normal relationship between face 204 and sidewall 202. Ascan be seen with respect to FIG. 11C, face 208 can extend at an anglefrom this rim to opening 206, and this angle can be measured to animaginary extension 212 as angle 210.

Referring next to FIG. 12A, a die 200 is shown with sidewalls 202 andrim 204. Referring to FIG. 12B, die 200 can have a recess 214 thereinabout opening 206. Recess or bore 214 can be contiguous with opening206. In accordance with example implementations and with reference toFIG. 12C, recess 214 can extend from the face 208 into the die alongmember or face 216 to a ledge 218, and then to opening 206. Opening 206has been described in relation to a single extrusion; however, opening206 can also be a larger opening that can be used in conjunction with amandrel to provide tubed material as extrusion products, for example

In accordance with example implementations and with reference to FIGS.13A-13C, die face 200 can include sidewall 202 and rim 204. As can beseen in FIG. 13B, recess 214 can be defined within die 200, and as shownin FIG. 13C, face 208 can be angled in relation to sidewall 202 and alsoinclude recess 214 having side face 216 extending to ledge 218.

Referring next to FIG. 14A, die face 200 can include sidewall 202 andrim 204. As can be seen, rim 204 can be substantially planar as shown inFIGS. 14B and 14C.

Referring next to FIGS. 15A-15B, in accordance with exampleimplementations, die 200 can be used to process feedstock material 220.Material 220 can be a single material or a mix of material as shown with# *, and as the ShAPE process proceeds, the material is sheared and/orplasticized to continue to form extrusion product 222. As can be seen,within recess 214 the material can mix. This mixing can provide for amore homogeneous or stable extrusion product 222.

Referring next to FIG. 16 , in accordance with another exampleimplementation, a die 200 is shown processing feedstock material 220.This die can have an angled face as well as shorter extensions extendingto a mandrel configuration, wherein mandrel 224 extends betweenextensions 226. This mandrel configuration with the shorter extensionscan provide for a more stable extrusion product 222 in the form of atube, for example. These extensions can be considered a bearing surface.

Referring next to FIGS. 17 and 18 , an example die 200 is shown havingface 208 as well as opening 206. In accordance with exampleimplementations, an extrusion product 222 is shown that can be providedutilizing this die 200. Additionally, the feedstock material can beseen, and the extrudate can be seen in accordance with FIG. 18 .

Referring next to FIG. 19 , an example die face is shown having a longbearing surface and without a counterbore or recess 214. As depictedFIGS. 19 and 20 represent two different scroll die configurations. FIG.19 depicts a die tool having a long bearing surface 1004 and nocounterbore 1006, while FIG. 20 depicts a die tool with a counterbore1002 and short bearing surface 226. As shown in FIG. 20 , the die facehas a short bearing surface 226 as well as a recess 214 within face 208.In accordance with example implementations and with reference to FIG. 21, utilizing these die faces with the angles and counterbores can providefor reduced extrusion force. As shown in FIG. 22 , these die faces canprovide reduced motor torque.

Referring next to FIG. 23 , a pair of die faces are compared, one havinga flat scrolled die face with a counterbore, and one including a conicaldie face or angled die face having angle 210 with a counterbore.Utilizing these die faces, reduced force is provided as shown in FIG. 24; reduced torque is provided as shown in FIG. 25 ; and reducedtemperature is provided as shown in FIG. 26 .

Referring next to FIG. 27 , utilizing the counterbore 214 and a shortbearing surface, a tubular extrusion product having a straight nicefinish can be provided as compared to a die face having a longer bearingsurface shown above.

Referring next to FIGS. 28-29 , again with a long bearing surface asshown in FIG. 28 , the extrusion product is fragile and twisted with arough surface, whereas the extrusion product prepared using a shortbearing surface and a recess is considered fully consolidated and astraight surface.

Referring next to FIGS. 30-31 , a comparison of extrusion productshaving different millimeters and different degrees is shown ranging fromgreater than 0 degrees to at least 45 degrees. Referring next to FIGS.32-34 , an example die face is shown in FIG. 32 , and an improved dieface is shown in FIG. 33 having a flat or planar rim 204 resulting in animproved product as shown in FIG. 34 . Referring next to FIGS. 35 and 36, data utilizing the scrolls of the present invention is disclosed.

In accordance with example implementations, materials can be engagedusing the ShAPE technology of the present disclosure. For example, Mgalloy ZK60 can be joined to Al alloy 6061, without forming an Mg₁₇Al₁₂interfacial layer. To accomplish this, the ShAPE™ process can bemodified to mix ZK60 and AA6061 into a fully consolidated rod having anAl rich coating as a corrosion barrier. Referring next to FIG. 37 , a 5mm diameter rod extruded from distinct Mg and Al pucks is shown in FIG.37 (A) with full consolidation shown in FIG. 37 (B), and FIG. 37 (C)shows a gradient in the composition (magenta Al map) between the Al richsurface and rod interior. Analysis showed the critical result that theMg₁₇Al₁₂ β-phase did not exist as an interfacial layer, rather the IMCwas highly refined and dispersed throughout the extrusion.

Referring to FIG. 38 , an example solid-phase method for joining Mg toAl extrusions in a butt configuration is shown. In accordance withexample implementations, separate Mg and Al billets can be interlockedto form a single billet that will be extruded using the ShAPE processfor example. As the die rotates and plunges to the right, an Mg alloyextrusion forms as the material is consumed. The rotating die thenpenetrates into the interlocking region of the two feedstock materialswhere Mg and Al are mixed and extruded simultaneously to form thedissimilar joint. Once the die penetrates past the interlocking regionof the two feedstock materials, an Al alloy extrusion forms as materialcontinues to be consumed. As shown in FIG. 39 , a multi-material rod orhollow-section extrusion can be fabricated absent of a brittle Mg₁₇Al₁₂interfacial layer is shown. The method can be used for rods and/or tubesof varying diameters.

The geometry of the interlocking region can be tailored to control thecomposition and transition length of the Mg—Al joint region. Thegeometric possibilities are many but two examples are shown in FIG. 38 ;one abrupt (flat pie shaped interface having complimentary portions 162a and 162 b that interlock to form interlocking region 163), and onegradual (triangular spokes interface having complimentary portions 164 aand 164 b that interlock to form interlocking region 165). The mostabrupt interface can be achieved with a flat interface between the Mgand Al billets.

In accordance with at least one implementation, with triangular spokedinterlocks 165, the composition of Mg in Al goes from 0% to 100% at arate depending on the number of spokes and angle of the triangle'svertex. This method has been used to demonstrate a transition length of37 mm to illustrate the concept. Because the joint is formed by mixingin the solid phase, an Mg₁₇Al₁₂ interfacial layer will not form. Rather,a gradient in chemical composition and also possibly grain size willform across the dissimilar interface with the intense shear refining anddispersing any Mg₁₇Al₁₂ second phase formations. The compositiongradient at the Mg—Al interface has a secondary benefit of also being agalvanically graded interface which can improve corrosion resistance.Referring to FIG. 40 Mg—Al tailor welded blanks are shown, with agalvanically graded interface, made by slitting and rolling tubes. Inaccordance with example implementations, rolling of 75 mil thick ZK60tubes down to 3 mil foils can be achieved using these tailor weldedblanks. Referring to FIG. 41 , using interlocked feed material of AA7075and AA6061, using the methods of the present disclosure, AA7075 can bebutt jointed with AA6061 as shown with an abrupt (pictured) or extendedtransition length.

Accordingly, an extrusion process for forming extrusion of a desiredcomposition from a feedstock is provided. The process can includeproviding feedstock for extrusion, and the feedstock comprising at leasttwo different materials. The process can further include engaging thematerials with one another within a feedstock container, with theengaging defining an interface between the two different materials asdescribed herein. The process can include extruding the feedstock toform an extruded product. This extruded product can include a firstportion that includes one of the two materials bound to a second portionthat can include one of the other two materials.

Accordingly, the interface between the two materials can interlock theone material with the other material and the geometry of the interlockcan define a ratio of the two materials where they are bound. This ratiocan be manipulated through manipulating the geometry of the engagement.For example, there could be a small amount of one of the materialsentering into a perimeter defined by the other of the two materials, andvice versa. In accordance with example implementations and specificexamples, one of the materials can be Mg and the other can be Al. Theprocess can also include where the one material is Mg ZK60 and the othermaterial is Al 6061. Accordingly, there could be one material that hasone grade and another that has another grade. For example, the materialcan be AA7075 and the other material can be AA6061. In accordance withexample implementations, these billets can be part of the feedstock andthe billets can be interlocked.

The extrusion feedstock materials may have a geometry that defines aratio of the two materials when they are extruded as bound extrusions.The feedstock materials can be aligned along a longitudinal axis, andaccording to example implementations this can be the extrusion axis. Theinterlock of the billets can reside along a plane extending normallyfrom the axis, and accordingly, the plane can intersect with bothmaterials.

In order to improve the formability of magnesium sheet materials, theinventors believe that the grain sizes should be less than 5 micronsand/or a weakened texture is desirable. It has been demonstrated thatthe novel Shear Assisted Processing and Extrusion (ShAPE) technology cannot only attain the aforementioned microstructure but also help with thealignment of the basal planes (i.e. texture). This technology can alsoreduce the size and uniformly distribute the second phase particles,which are believed to impede the formability of sheets. In accordancewith example implementations, extruded tubes of Mg can be slit open androlled into the sheet. Extruded tubes of magnesium (ZK60 alloy) usingthe ShAPE process can be provided which can be 50 mm in diameter and 2mm in wall thickness, or another diameter and wall thickness. Thesetubes can be slit open in a press and then rolled parallel to theextrusion axis, for example.

Referring next to FIG. 42 , in particular embodiments, Mg sheets can beprovided that are not common in mass produced vehicles, for example. Theproduction of these sheets can include the use of rolling of ShAPEproduced and open extruded tubes. In accordance with exampleimplementations, and with reference to FIG. 42 , an example rolling mill130 is shown. In accordance with example implementations, rolling mill130 can have conveyer 132 but have a sheet 134 of a first thickness andafter passing through mill 130, the sheet 134 can be a sheet 136 of asecond thickness. In accordance with example implementations, thisrolling can be cold rolling, hot rolling, or twin rolling. ShAPEextrusions such as ShAPE tubing can provide a feedstock for subsequentrolling that can provide differentiated and/or advantageous grain size,second phase size and distribution, and/or crystallographic texture whencompared to conventional feedstocks for rolling.

Referring next to FIG. 43 , a series of depictions are showndemonstrating a ShAPE fabricated Mg ZK60 tube and the open tubethickness as well as the rolled tube rolled hot to a desired thickness.In accordance with example implementations, the rolled tube can beannealed between passes at between 420° C. and 450° C. for 5 minutes,and can be performed without a twin roll casting if desirable.

Referring next to FIGS. 44A and 44B, in accordance with exampleimplementations and as described herein, these Mg billets such as theZK60 billet can be produced about a chilled mandrel as disclosed herein,with frictional heat to produce a tube having an extrusion direction andbasal planes about that extrusion direction. In accordance with exampleimplementations, these materials can be anisotropic which can make themquite robust.

Referring next to FIG. 45 , a series of passes are shown from zeropasses all the way to 16 passes of a Mg sheet. In FIG. 46 a 0.005 inchthickness sheet is shown and demonstrated the flexibility and robustnessin the accompanying two figures. In accordance with exampleimplementations and with reference to FIG. 47 , reduction per rollingpass has been plotted, and as can be seen, after about 5 rolling passes,the thickness remains uniform, but after 10 rolling passes, there can bea reduction in thickness of up to 60%. Such large reductions per passare difficult to impossible to achieve with hot rolling of conventionalMg feedstocks intended for subsequent rolling operations.

Referring next to FIG. 48A, according to an example implementation ofthe present disclosure, upon ingot formation of an as-cast billet, forexample, the as-cast billet can be heated prior to extrusion, or notheated prior to extrusion. As FIG. 48A shows, this series of steps doesnot include a homogenization step. To the extent it may includehomogenization as detailed with reference to FIG. 48B, thathomogenization will not be performed to the length and extent that theprior art methods dictate and billet pre-heating in a furnace may beeliminated and accomplished entirely by the ShAPE process.

Accordingly, the methods of the present disclosure for preparing anextruded product from a solid billet can include providing an as-castbillet for extrusion. These as-cast billets are billets that have notbeen prepared to remove microfissures, convert phases, homogenize thebillet to have a more uniform consistency throughout prior to extrusion.Billets with some amount of stress relief and phase conversion may alsobe used. To have a uniform consistency, convert phases, and removal ofmicrofissures, the present disclosure provides applying a simultaneousrotational shear and axial extrusion force to the as-cast billet toplasticize the as-cast billet. During this performance of the method,the materials themselves are homogenized and/or plasticized, and themethod can include extruding the plasticized as-cast billet with anextrusion die to form an extruded product. As such the metallurgicalfunctions of stress relief, phase conversion, and homogenization may inpart, or entirely, be accomplished by the ShAPE process.

As detailed herein, this can include the ShAPE technology describedabove. In accordance with an example implementation, the as-cast billetcan be heated for approximately 17 hours between about 200° C. and 490°C. without a subsequent homogenization step prior to applying thesimultaneous rotational shear and axial force. Additionally, where heatis applied, it can be applied in steps at predefined temperatures forpredefined durations of time. For example, the temperature changebetween two of the steps can be about 260° C., or between two of thesteps can be about 30° C. in temperature change, or other temperaturedifferences combinations. Even when applying this heat for this time,the as-cast billet may not be homogenized prior to applying thesimultaneous rotational shear and axial extrusion force to the as-castbillet. Accordingly, the as-cast billet can include intermetallic and/ordistinct microstructures prior to the application of the rotationalshear and axial extrusion force.

Referring to FIG. 48B, ingot formation can be performed, and then theas-cast billet can be homogenized prior to extrusion with or withoutpre-heating. For example, the billet can be provided for extrusion, butwhile maintaining a majority of the billet below 100° C. prior toextrusion, a simultaneous rotational shear and axial extrusion force canbe applied to one end of the billet to plasticize the one end of thebillet. The plasticized one end of the billet can form an extrudedproduct using the die. The billet itself may be as-cast or it may behomogenized in accordance with prior art techniques. However, the billetitself will not be heated to greater than 100° C. before being extruded.In accordance with example implementations, the billet can be maintainedat about ambient temperature prior to starting the extrusion process.

With regard to FIG. 48C, the ingots can be formed and then extrusion cantake place. Accordingly, as shown, ingot formation can provide anas-cast billet complete with microstructures and portions that arenon-homogenous, and then provided directly for extrusion utilizing themethods of the present disclosure without stress relief, phaseconversion or pre-heating the as-cast billet to a temperature great than100° C. prior to starting the extrusion process.

Referring next to FIG. 49A, as is shown, in at least one exampleimplementation a portion of homogenization can be performed but asignificant amount of time can be removed. As can be seen, at least 20hours is removed. FIG. 49B shows an additional thermal treatmentsequence where homogenization is also eliminated and only stress reliefand phase conversion are needed.

Referring next to FIG. 50 , data of material prepared from AA7075as-cast billets is provided with ultimate yield and strength, andelongation percentage, and a die temperature as shown when heat treatedto the T6 condition after extrusion. As is shown, the die temperaturecan be as low as approximately 340° C. but can be as high as 480° C.Extrusion below 340° C. is also possible. However, this temperaturerange does not apply to the entirety of the billet; it only applies tothe very end of the billet as it is being extruded and plasticized.Additionally, these methods can be performed on any number of materials,but these example specific materials are AA7075 materials where ASTM andASM standard values are exceeded for T6 properties. As detailed in thisspecification, a range of materials can be utilized for these processesand include magnesium, aluminum, and all others listed herein.

As described above, in a conventional linear force extrusion process,the billet itself is pre-heated in a furnace such as a jet billet logfurnace to soften the billet to assist with the plasticization of thebillet during extrusion. The present disclosure does not require suchbillet pre-heating in a furnace, and the only heating taking placeoccurs at one end of the billet as a result of the heat generated by theextrusion process, while a portion of the remainder of the billetremains at a lower temperature than the die/billet interface, forexample.

Referring next to FIG. 51 , an example extruded product is shown whichdemonstrates the uniformity and surface finish of the product in theas-extruded condition having been extruded from as-cast billets that didnot undergo homogenization or billet pre-heating.

Referring next to FIG. 52 , an example extrusion process includesextrusion and solution heating. However, this solution heating issubstantially different than the solution heating of the prior art. Ascan be seen in FIG. 53 , the solution heating with aluminum alloy 6063with T6 heat treatment can include solution heat treating for 1 hour at530° C. quenching, and then artificially aging at 177° C. for 8 hours.With T5 heat treatment, there is no solution heat treating, and there isno quench, and the artificial aging can take place at 177° C. for lessthan 8 hours.

Now it must be noted that typically in the prior art, a requirement ofsubstantially more time is required for the artificial aging. Inaccordance with example implementations of the present disclosure, peakhardness can be obtained after artificially aging the extruded productfor less than 10 hours and in general lower time than is standard andsolution heat treat times and temperature below that specified in ASTMstandards.

In effect, the ShAPE process is able to manufacture AA6063 in the T5condition that has strength properties well above the ASTM and ASMstandards for AA6063 in the T5 condition. Strength properties of AA6063made by ShAPE in the T5 condition exceed the ASTM strength values forAA6063 in the T6 condition and approach the ASM strength properties ofAA6063 in the T6 condition. Accordingly, excellent properties areobtained without the need for solution heat treating and quenching whenextruding with ShAPE.

Additionally, these methods can be performed on any number of materials,but these example specific materials are AA6063 materials and near T6properties can be achieved using the T5 conditions. As indicated in thisspecification, a range of materials can be utilized for these processesand include magnesium, aluminum, and all others listed herein.

Referring next to FIG. 53 , data is shown that demonstrates thereduction in solution heat treating time and temperature when solutionheat treating is performed at 450° C. for 15 minutes by flash annealing,while the conventional ASTM standard is heat treating at 465° C. for 40minutes. Flash annealing is performed on the extruded product under UVradiation from lamps such as high energy lamps.

As shown, the ShAPE extruded product can perform as well with lowertemperature and time. As shown in FIG. 53 , AA7075 Rod extrusion isprovided, demonstrating like preparation without the additional time andat a lower temperature.

Referring to FIG. 54 , Rod extrusion for AA6061 is shown thatdemonstrates a much shorter solution heat treatment time, 530° C. for 15minutes rather than the ASTM standard of 530° C. for 120 minutes ispossible with flash annealing of ShAPE extrusions. As can be seen, thatwhen the solution heat-treatment time has been reduced from 2 hours to15 minutes at 530° C. by flash annealing that like material hardness isachieved after the same artificial aging time at 530° C. for longertimes.

Referring next to FIG. 55 , data for two different extrusion trials isshown that demonstrates the decreasing of artificial aging time usingthe ShAPE process from 24 hours to 5-10 hours for AA7075 after a typicalsolution heat treatment of 480° C. for 24 hours for both of theextrusion trials shown. Accordingly, the present disclosure provides foraging the extruded product for approximately 3-10 hours or ascontemplated.

Referring next to FIGS. 56A and 56B, the extrusion is shown in FIG. 56Ato go right to aging, and then also in FIG. 56B, solution heat treatingand aging can be used as well.

Referring next to FIG. 57 , data is presented that demonstrates the peakhardness of the material can be achieved after 3 hours of aging at 120°C. It must be noted that the ASTM handbook specifies a minimum of 22hours at 120° C. for peak artificial aging of AA7075. Accordingly, thepresent disclosure provides methods that can be used to significantlyreduce aging. In accordance with example implementations, the presentdisclosure provides methods that significantly reduce the temperatureand energy required and time necessary to prepare satisfactory extrusionproducts.

While the largest applications of aluminum alloys is as cast or wroughtarticles, the powder metallurgy (PM) route has recently been utilized toproduce net- or near-net-shape parts. This route is economicallycompetitive for relatively small parts which would otherwise requireextensive machining if fabricated from a bulk alloy. Additionally,aluminum PM benefits from more homogenous microstructures than wroughtarticles, and unique chemistries realized by rapid solidification ormechanical alloying. However, the conventional press-and-sinter approachpresents great difficulty for aluminum alloys due to a tenacious oxidelayer preventing full powder bonding, resulting in comparatively lowstrength and ductility. Other more complicated powder densificationprocesses, which typically require multiple steps (canning, degassing,compaction, and extrusion or forging), break the powder oxide layers bysevere deformation, thus resulting in near-theoretical density and goodmechanical properties.

Referring next to FIGS. 56A-57 , extruded material using the apparatusand/or methods described herein can be utilized without additionalcostly post extrusion treatment processes, although typical quenchingcan be employed during the extrusion process. As is shown in FIGS. 56Aand 56B, extruded material can be treated with aging and/or solutionheating and then aging. The aging process for each of these methodstakes a substantial amount of time. As shown in FIG. 57 , peak hardnessof material extruded using ShAPE can be achieved after 3 hours at 120°C.

The stock material extruded using ShAPE can include powder material,casting material, and/or flake, powder, or scrap material. The materialcan be a solid billet or mixture of solid billets. The solid materialcan include one or more of the materials listed herein.

The extruded material can have a hardness of at least 155 HV after 3hours of aging. Additionally, the extruded material may be solutionheated and then aged. However, the aging of the extruded material aftersolution heating is performed for less than 3 hrs.

Powder metallurgy (PM) of high strength aluminum (Al) alloys typicallyrequires multiple process steps prior to extrusion. In general,compacting powder into a densified billet or canning powder in a sealedcontainer are the primary methods used to ready material for PMextrusion and have endured as the most widely utilized approaches forhigh strength Al alloys. For powder canning, typical steps includeloading powder into a can, degassing, sealing the can, and heating. Forpowder compaction, typical steps include degassing, hot or coldisostatic pressing, and heating the densified billet. Eliminating any ofthese steps could make PM more cost effective. The compaction andcanning processes have been researched extensively for high strength PMAl alloys.

Utilizing the apparatus and/or methods of the present disclosure,frictional heating of billet material in substantially powder form(most, if not all of the billet material is in powder form) can belocalized to the die face, and spiral grooves, or a flat face withoutgrooves, draw billet material towards the hollow center of the dieutilizing (ShAPE). As the powdered billet is consolidated by compressiveand shear forces within the deforming material (plasticizing) andfrictional heating at the die face and within the deforming material,solid material is extruded. In accordance with at least some embodimentsof the disclosure, low extrusion forces are required compared toconventional extrusion. Additionally, by directly creating solidextrudate from loose powder, many of the complicated processing stepsnecessary for the other methods are eliminated, presenting a scalablemethod to produce high strength aluminum alloys. These methods can beutilized successfully to extrude magnesium flakes and/or a gas-atomizedaluminum alloy powder containing 12.4 wt. % transition metal. The ShAPEprocess can extrude hollow tubular profiles directly from powder whichis not readily possible with conventional powder metallurgy extrusion.

TABLE 4 Mechanical properties of extruded powder materials (ShAPE andnon-ShAPE) Temperature Yield Strength Method (° C.) (MPa) Elongation (%)PM Extrusion Ambient 375-405 4.5-9.0 ShAPE Extrusion Ambient 380 ± 1315.74 ± 2.5 ShAPE Extrusion 200/300 314/238 9.5/9.4 Testing performedper ASTM B557

As shown above in Table 4, the ShAPE materials demonstrated superiormechanical properties when compared to non-ShAPE extruded materials. Inaccordance with example implementations and with reference to FIGS.58-60 , the ShAPE materials improved the mechanical properties of thepowdered materials they were manufactured from. For example, allmaterials were refined with ShAPE to allow for more mechanically strongrealignment of elements. This alignment of elements provides superiorstrengthened matrices as shown.

Accordingly, methods for preparing an extruded material by shearassisted processing and extrusion from a powder billet are provided. Themethod can include providing a billet of material in substantiallypowder form. This powder can be considered a loose powder (unpacked, ornoncompacted). The powder can include one or more of Al, Mg, Fe, Si,and/or Zr. The billet material can have a maximum particle size of 100um, but particle sizes greater than 100 um can be utilized as well. Thepowder can include an oxide or powder component

The method can include applying both axial and rotational pressure tothe material to deform at least some of the material, and extruding thematerial to form an extruded material as described herein. Particularly,an extrusion die defining spiral grooves can be used.

The extruded material include an alloy and/or can have a tensilestrength from about 220 MPa to about 360 MPa. Additionally, the extrudedmaterial can have a hollow profiles (i.e. hollow tubes that arecircular, non-circular, or even have multiple hollow zones), as shownand described herein.

The ShAPE process can be used to prepare product materials from Al—Mg—Zrpowder. The application of ShAPE to high performance aluminum powderscan eliminate process steps used during PM extrusion. Specifically,canning, degassing, sealing, charge pre-heating, cold/hot isostaticpressing, extrusion, and decanning used in PM extrusion can beeliminated and replaced by container filling, compaction, and subsequentShAPE processing. Process parameters (rpm, feed rate, forge force andtemperature) can provide for the extrusion of fully consolidatedextrudates (extruded material).

High performance bulk material from aluminum powders that include alloyscan be fabricated. By combining the versatility of the ShAPE process andthe far-from-equilibrium microstructures of the gas-atomized Al—Mg—ZrAddalloy powders, PM parts can be designed and developed for massapplications from precipitation-strengthened aluminum alloys withoutstanding coarsening resistance that have high thermal stability.

ShAPE can increase extrusion speeds, for example in the preparation ofaluminum alloys. The ShAPE process parameters and tooling enable fastextrusion speed for aluminum alloys, which traditionally have beendifficult to extrude. Conventional extrusion speed(s) for aluminumalloys in series 2XXX and 7XXX are generally 1-2 meters/minute.

The ShAPE processes and methods described herein increase extrusionspeed(s), which can, in some examples, reduce the cost of 7XXX (7series), 2XXX (2 series), and other alloy extrusions, aluminum andnon-aluminum. The ShAPE process has been advanced for fabrication ofAA7075 extrusions at extremely high speed(s) compared to conventionalextrusion. For example, a speed of 7.4 meters/minute has been achievedwith mechanical properties equal to, or in excess of, propertiesachieved from slow speed conventional extrusion (i.e., the ASTM B241standard and/or consistent with the typical values in the ASM handbook).

Accordingly, methods for preparing extruded material by shear assistedprocessing and extrusion are provided that can include applying bothaxial and rotational pressure to stock material to form an extrudedmaterial at a rate between 2 and 13 m/min in some implementations, 3 and13 m/min in others, and 7 and 13 m/min in still others. As describedherein, the stock material or billet material can be defined bycastings, or chunks of material randomly aligned. This material can besourced as recycled material and can include Al and/or any of thematerials listed herein.

The methods can include maintaining a temperature of the die face below420° C.

The extruded material has a tensile strength between 500 and 580 MPa, ayield strength between 420 and 500 MPa, and/or an elongation % between12 and 18.

Homogenized AA 7075 castings were machined into billets having an innerdiameter (ID) of 10.1 mm, outer diameter (OD) of 31.8 mm, a length of100 mm. Extrusions were fabricated using a ShAPE machine manufactured byBOND Technologies capable of 900 kN axial force and torque of 3000 Nm at500 rpm. The linear speed of tailstock is 0.36 meters/min which gives anextrusion speed of 7.4 meters/min for the extrusion ratio of 20.6, forexample. Speeds up to 12.2 meters per minute and beyond have beenachieved for 7XXX and 2XXX. In conventional extrusion, a high peak forceis required at the beginning of direct and indirect extrusion processes,which is known as the breakthrough force. This is because a givenpressure is required to start deforming the material, which drops to alower pressure once the material starts flowing. This is not desirablebecause the peak breakthrough force dictates the required capacity ofthe extrusion press. Lower force means a smaller extrusion press andlower operating cost. The origin of the work is that the research teamwas trying to keep the force as low as possible to get the highest speedextrusion possible out of the research scale ShAPE machine which islimited to 900 kN.

Breakthrough force was eliminated by ramping ram speed (generallyramping up) and rotational speed of the die (generally ramping down). Indoing so, these parameters are balanced to generate heat sufficient tolocally soften the billet material ahead of the die. Because thematerial that the die encounters is always soft from the very beginningof the stroke, the force gently rises to steady state for shearextrusion. This is in contrast to conventional extrusion where forcerises quickly to a peak force as the die encounters cooler material andthen reduces to lower the steady state value.

As can be seen in FIGS. 61 and 62 , the initial axial force can beramped to a steady state axial force, and/or the rotational rpms can bedecreased during the ramping. This data is shown with speed, power, andtorque data in FIGS. 62-65 . Particularly, in these FIGS., as the axialforce is decreased, the tool temperature increases.

Table 5 below provides a list of example alloys and a rating ofextrusion difficulty.

TABLE 5 Alloy Difficulty 1000 77 1100 86 6063 100 3005 106 3003 112 6105134 4047 128 3105 126 6061 151 5005 154 7004 157 2011 171 3004 180 6082197 2014 202 5052 229 5056 232 2024 247 5054 265 7150 269 7050 280 5083281 5182 293 5456 300 7075 316

In compliance with the statute, embodiments of the invention have beendescribed in language more or less specific as to structural andmethodical features. It is to be understood, however, that the entireinvention is not limited to the specific features and/or embodimentsshown and/or described, since the disclosed embodiments comprise formsof putting the invention into effect. The invention is, therefore,claimed in any of its forms or modifications within the proper scope ofthe appended claims appropriately interpreted in accordance with thedoctrine of equivalents.

1. A method for preparing an extruded material by shear assistedprocessing and extrusion from a powder billet, the method comprising:providing a billet of material in substantially powder form; applyingboth axial and rotational pressure to the material to deform at leastsome of the material; and extruding the material to form an extrudedmaterial.
 2. The method of claim 1 wherein the billet material is loosepowder.
 3. The method of claim 1 wherein the billet material comprisesAl.
 4. The method of claim 1 wherein the billet material comprises oneor more of Al, Mg, Fe, Si, and/or Zr.
 5. The method of claim 4 whereinthe extruded material comprises an alloy.
 6. The method of claim 1wherein the billet material in powder form can have a maximum particlesize of 100 um.
 7. The method of claim 1 wherein the billet material inpowder form can have a particle size greater than 100 um.
 8. The methodof claim 1 further comprising using an extrusion die defining spiralgrooves.
 9. The method of claim 1 wherein individual particles of thepowder include an oxide or ceramic component.
 10. The method of claim 1wherein the extruded material has a tensile strength from about 220 MPato about 360 MPa. 11-20. (canceled)
 21. A method for preparing extrudedmaterial by shear assisted processing and extrusion, the methodcomprising: applying both axial and rotational pressure to stockmaterial to form an extruded material; and aging the extruded materialfor less than 3 hours.
 22. The method of claim 21 wherein the stockmaterial is in powder form.
 23. The method of claim 21 wherein the stockmaterial is defined by castings.
 24. The method of claim 21 wherein thestock material comprises powder, flake, chip, or scrap.
 25. The methodof claim 21 wherein the stock material comprises Al.
 26. The method ofclaim 21 wherein the extruded material has a hardness of at least 155 HVafter the 3 hrs.
 27. The method of claim 21 further comprising solutionheating the extruded material before the aging.
 28. A method forpreparing extruded material by shear assisted processing and extrusion,the method comprising: providing a stock material for shear-assistedextrusion; and applying both axial and rotational force to the stockmaterial to form an extruded material, wherein the axial force does notdecrease during the extrusion.
 29. The method of claim 28 furthercomprising initiating an initial axial force upon a stock material;maintaining a steady state axial force upon the stock material; andreducing the axial force upon stock material depletion.
 30. The methodof claim 29 wherein the stead state axial force is greater than theinitial axial force.
 31. The method of claim 29 further comprising atransition between the initial axial force and the steady state axialforce, the transition having a position slope when plotted.
 32. Themethod of claim 28 further comprising ramping the initial axial force tothe steady state axial force.
 33. The method of claim 32 furthercomprising decreasing rotational rpms while increasing ramping of ramspeed.
 34. The method of claim 29 further comprising maintaining a dieface temperature during steady force application at a substantiallyconstant temperature.
 35. The method of claim 34 wherein the temperatureis about 400° C.